EP1096029B1 - Hochfeste heisstauchzinkbeschichtete stahlplatte mit hervorragenden duktilitätseigenschaften und verfahren zu deren herstellung - Google Patents

Hochfeste heisstauchzinkbeschichtete stahlplatte mit hervorragenden duktilitätseigenschaften und verfahren zu deren herstellung Download PDF

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Publication number
EP1096029B1
EP1096029B1 EP00919136A EP00919136A EP1096029B1 EP 1096029 B1 EP1096029 B1 EP 1096029B1 EP 00919136 A EP00919136 A EP 00919136A EP 00919136 A EP00919136 A EP 00919136A EP 1096029 B1 EP1096029 B1 EP 1096029B1
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Prior art keywords
steel sheet
temperature
mass
cooling
sec
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French (fr)
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EP1096029A4 (de
EP1096029A1 (de
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Takashi Technical Research Labs. KOBAYASHI
Kei Technical Research Laboratories SAKATA
Akio Mizushima Works SHINOHARA
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the present invention relates to a high-strength galvanized steel sheet having improved ductility when galvanized in a continuous galvanizing line.
  • a structure strengthening type steel sheet with a composite structure of ferrite and a low-temperature transformation phase As a high-strength steel sheet excellent in ductility, there is suggested a structure strengthening type steel sheet with a composite structure of ferrite and a low-temperature transformation phase.
  • a dual phase type steel sheet having a composite structure of ferrite and martensite is typical of this structure strengthening type steel sheet.
  • a high-ductility steel sheet using transformation-inducing plasticity resulting from retained austenite has become practicable.
  • An example of a method for producing a structure strengthening type high-strength galvanized steel sheet in a continuous galvanizing line is a method that makes it easy to produce a low-temperature transformation phase, such as martensite by adding an alloying element causing a rise in hardenability, such as Cr or Mo, in a great amount to the steel.
  • an alloying element causing a rise in hardenability, such as Cr or Mo in a great amount to the steel.
  • Japanese Patent Application Publication No. 62-40405 suggests a manufacturing method of a structure strengthening type alloyed galvanized steel sheet having high-strength, using a continuous galvanizing line for heating sheet steel comprising C: 0.005-0.15%, Mn: 0.3-2.0%, and Cr: 0.03-0.8% to a temperature between Ac 1 transformation temperature and Ac 3 transformation temperature, subjecting the steel sheet to galvanizing treatment in the middle of cooling the steel sheet, subjecting the steel sheet to alloying treatment wherein the steel sheet is heated to a temperature between 500°C and Ac 1 transformation temperature, and subsequently cooling the steel sheet to 300°C.
  • This manufacturing method of alloyed galvanized steel sheet having high-strength is characterized in that the cooling after the heating to a temperature between Ac 1 transformation temperature and Ac 3 transformation temperature, and the cooling to 300°C after the alloying treatment are performed at cooling rates that are not less than a critical cooling rate defined by an equation related to the Cr and Mn content.
  • a dual phase type steel sheet comprising, in a ferrite base, a low-temperature transformation structure made mainly of martensite is thereby prepared and a steel sheet having an alloyed galvanized layer thereon is produced.
  • Japanese Patent Application Laid-Open No. 6-93340 suggests a manufacturing method of a high-strength, alloyed, galvanized steel sheet comprising heating and holding at not less than recrystallization temperature and not less than Ac 1 transformation temperature, subsequent rapid cooling to not more than Ms point temperature, heating at a temperature that is not less than the Ms point temperature and that is not less than galvanizing-bath temperature and alloying-furnace temperature, and subsequent immersion into a galvanizing-tank.
  • Japanese Patent Application Laid-Open No. 6-108152 suggests a manufacturing method of a high-strength, alloyed, galvanized steel sheet excellent in bendability, comprising a recrystallization annealing step involving holding at a temperature from (Ac 3 transformation temperature - 50°C) to 900°C for at least 1 second or more, a step of performing galvanization, and a subsequent step of conducting reheating treatment at a temperature from Ac 1 transformation temperature to 250°C (both inclusive), in which cooling is performed from a temperature higher than Ms point temperature to the Ms point temperature or lower at a cooling rate that is not less than a critical cooling rate, which depends on the amounts of alloying elements, after the recrystallization annealing step and before the reheating treatment step.
  • Both of the techniques described in the Japanese Patent Application Laid-Open No. 6-93340 and the Japanese Patent Application Laid-Open No. 6-108152 are manufacturing methods of a high-strength, alloyed, galvanized steel sheet in which the steel sheet is quenched from an austenite temperature range to a temperature not more than Ms point temperature before galvanizing or alloying treatment to produce a steel sheet having martensite structure and then this is reheated to produce tempered martensite.
  • the present invention provides a high-strength galvanized steel sheet which has sufficient ductility for a raw material of car parts and well-balanced strength and elongation and a manufacturing method thereof, solving the above-mentioned problems in the prior art.
  • the high-strength galvanized steel sheet of the present invention is desirably produced using a continuous galvanizing line.
  • JP-A-02 175 817 discloses a hot rolled plate of steel having a composition as that of the present invention and a composite structure of tempered martensite and fine martensite, which structure is obtained by hot rolling, quenching, releating and quenching again and secures high tensile strength and cold formability cold rolling and galvanizing are not provided.
  • the structure of steel sheet in order to make the structure of steel sheet up to a composite structure comprising tempered martensite, retained austenite, and the balance of ferrite and a low-temperature transformation phase, the structure of steel sheet whose chemical composition is adjusted within a given range is first made to a microstructure having lath-like martensite and then the steel sheet is subjected to reheating and galvanizing treatments under given conditions in a continuos galvanizing line.
  • the steel sheet can be made to have the above-mentioned composite structure comprising tempered martensite, retained austenite, and the balance of ferrite and the low-temperature transformation phase, thereby coming to a high-strength galvanized steel sheet that is very good in ductility.
  • the present invention has been made on the basis of the above-mentioned findings.
  • a first present invention is a galvanized steel sheet having excellent ductility, characterized by comprising, as a topmost layer of the steel sheet, a galvanized layer or an alloyed galvanized layer, the steel sheet having a composition comprising C: 0.05-0.20 mass %, Si: 0.3-1.8 mass %, Mn: 1.0-3.0 mass %, Fe of the balance and inevitable impurities, and comprising a composite structure having tempered martensite, retained austenite, ferrite and a low-temperature transformation phase, the tempered martensite being contained in an amount of 20% or more by volume, and the retained austenite being contained in an amount of 2% or more by volume.
  • the first present invention not only the above-mentioned composition but also one or more groups selected from the following groups (a)-(d) may be comprised:
  • a second present invention is a method for manufacturing a galvanized steel sheet characterized by performing successively a primary step of subjecting steel sheet having a composition comprising C: 0.05-0.20 mass %, Si: 0.3-1.8 mass %, Mn: 1.0-3.0 mass %, Fe of the balance and inevitable impurities to primary heat treatment in which the steel sheet is held at a temperature of (Ac 3 transformation temperature -50°C) or higher for 5 seconds or more, and then cooling the steel sheet to a temperature that is not more than Ms point temperature at a cooling rate of 10 °C/sec. or more; a secondary step of subjecting the steel sheet to secondary heat treatment in which the steel sheet is held within a temperature range between Ac 1 transformation temperature and Ac 3 transformation temperature for 5-120 sec.
  • the tertiary step is preferably a step of subjecting the steel sheet to galvanizing treatment to form the galvanized layer on the surface of the steel sheet, reheating the steel sheet to a temperature range of 450 to 550°C so as to subject the galvanized layer to alloying treatment and, after the alloying treatment, cooling the steel sheet to 300°C at a cooling rate of 5 °C/sec. or more.
  • the steel sheet is made to hot-rolled steel sheet that has been subjected to final hot rolling at a temperature that is (Ar 3 transformation temperature -50°C) or higher, and the primary step is replaced by a hot-rolled steel sheet structure adjusting step of cooling the steel sheet rapidly to a temperature that is Ms point temperature or lower at a cooling rate of 10°C/sec. or more after the final hot rolling.
  • the high-strength galvanized steel sheet of the present invention is a galvanized steel sheet having, as a topmost layer thereof, a galvanized layer or an alloyed galvanized layer.
  • % in the composition means mass %.
  • C is an essential element for making the strength of any steel sheet high and has an effect for producing retained austenite and the low-temperature transformation phase.
  • C is an indispensable element.
  • the C content is below 0.05%, desired high-strength cannot be obtained.
  • it is over 0.20% weldability comes to deteriorate. Therefore, the C content is limited within a range of 0.05 to 0.20%.
  • Mn has effects for strengthening steel by solid-solution hardening, improving hardenability of steel, and promoting the production of retained austenite and the low-temperature transformation phase. Such effects can be recognized if the Mn content is 1.0% or more. On the other hand, if Mn is contained in an amount over 3.0%, the effects are saturated and the effects matching with the content cannot be expected. Thus, costs rise. Therefore, the Mn content is limited within a range of 1.0-3.0%.
  • Si has effects for strengthening steel by solid-solution hardening, and stabilizing austenite to promote the production of retained austenite. Such effects can be recognized if the Si content is 0.3% or more. On the other hand, if Si is contained in an amount over 1.8%, capability of being galvanized deteriorates remarkably. Therefore, the Si content is limited within a range of 0.3-1.8%.
  • the steel sheet of the present invention may comprise not only the above-mentioned composition but also one or more selected from the following groups (a)-(d).
  • Cr and Mo are elements having effects for improving hardenability of steel and promoting the production of the low-temperature transformation phase. Such effects can be recognized if one or two selected from Cr and Mo are contained in a total amount of 0.05% or more. On the other hand, if they are contained in a total amount over 1.0%, the effects are saturated and the effects matching with the content cannot be expected. Thus, economical disadvantage is caused. Therefore, the total amount of one or two selected from Cr and Mo is desirably limited within a range of 0.05-1.0%.
  • B is an element having an effect for improving hardenability of steel. If necessary, B is contained. However, if the B content is over 0.003%, the effect is saturated. Therefore, the B content is desirably limited to 0.003% or less. More desirable content is 0.001-0.002%.
  • Ti, Nb and V have effects for making carbide, nitride and attaining high strength of steel by precipitation hardening. If necessary, these may be added. Such effects are recognized in the case that the total amount of one or more selected from Ti, Nb and V is 0.01% or more. On the other hand, if they are contained in a total amount of more than 0.1%, too high strength is attained so that ductility deteriorates. Therefore, the total amount of one or more selected from Ti, Nb and V is preferably limited within a range of 0.01-0.1%.
  • Ca and REM have an effect for controlling the shape of sulfide inclusion, thereby having an effect for improving stretch-flanging property of any steel sheet. Such an effect is saturated if the total amount of one or two selected from Ca and REM is over 0.01%. Therefore, the total amount of one or two selected from Ca and REM is preferably limited to 0.01% or less.
  • the steel sheet used in the present invention comprises Fe of the balance and inevitable impurities as other than the above-mentioned chemical components.
  • the inevitable impurities may be as follows: Al: 0.1% or less, P: 0.05% or less and S: 0.02% or less.
  • the steel sheet of the present invention is a steel sheet having the above-mentioned chemical composition and comprising a composite structure of tempered martensite, retained austenite, ferrite and a low-temperature transformation phase.
  • the tempered martensite in the present invention means a phase produced when lath-like martensite is heated and held within a temperature range (from Ac 1 transformation temperature to Ac 3 transformation temperature) for a short time.
  • the tempered martensite is a phase having microstructure which inherits the shape of the lath-like martensite before tempering.
  • the tempered martensite is made soft by tempering to have sufficient plastic deformation ability. Therefore, it is a phase effective for an improvement in ductility of any high-strength steel sheet.
  • the steel sheet of the present invention comprises 20% or more by volume of such a tempered martensite phase. If the amount of the tempered martensite is below 20%, remarkable effect of improving ductility cannot be expected. Therefore, the amount of the tempered martensite in the composite structure is limited to 20% or more. If the amount of the tempered martensite is over 80%, it becomes difficult to make the strength of the steel sheet high. Thus, the amount is preferably set to 80% or less.
  • Retained austenite is transformed to martensite by strain induction upon working and has an effect for dispersing locally-applied working strain widely to improve ductility of a steel sheet.
  • the steel sheet of the present invention comprises 2% or more by volume of such retained austenite. If the amount of retained austenite is below 2%, a remarkable improvement in ductility cannot be expected. Therefore, the amount of retained austenite is limited to 2% or more.
  • the amount of retained austenite is preferably 5% or more. A larger amount of retained austenite is more preferable. However, in the steel sheet of the present invention produced through the heat history in a continuous galvanizing line, the amount is practically 10% or less.
  • tempered martensite and retained austenite are ferrite and a low-temperature transformation phase.
  • Ferrite is a soft phase containing no iron carbide, and has a high deformation ability to improve ductility of a steel sheet.
  • the steel sheet of the present invention preferably comprises 30% or more by volume of ferrite. If the amount is below 30%, the improvement in ductility is a little. On the other hand, if the amount is over 70%, it becomes difficult to make the strength of the steel sheet high. Therefore, the amount of ferrite is preferably set to 70% or less.
  • the low-temperature transformation phase referred to in the present invention means martensite that is not tempered or bainite. These low-temperature transformation phases are produced in the cooling stage in or after the secondary step in the manufacturing method of the present invention. Both of martensite and bainite are hard phases to increase the strength of a steel sheet. The amount of the low-temperature transformation phase is not especially limited. This phase is appropriately distributed in accordance with the strength of the steel sheet. In order to increase the strength sufficiently, the low-temperature transformation phase is preferably martensite, which is hard.
  • Ferrite which is a soft phase
  • the low-temperature transformation phase which is a hard phase
  • the tempered martensite and retained austenite constitute a composite structure, so that microstructure is made wherein soft phases and hard phases are mixed.
  • the high-strength galvanized steel sheet of the present invention is a galvanized steel sheet wherein a galvanized layer or an alloyed galvanized layer is formed on the topmost layer of the steel sheet having the above-mentioned composition and the above-mentioned composite structure.
  • the coating-weight of the galvanized layer may be appropriately decided in accordance with the demand degree of corrosion resistance for use parts, and is not especially defined.
  • the thickness (the coating-weight) of the galvanized layer is preferably 30-60 g/m 2 .
  • molten steel having the above-mentioned chemical composition is produced, and is cast in a usual known manner.
  • the resultant slab is hot rolled, or further cold rolled in a usual known manner to prepare steel sheet. If necessary, the steel sheet is subjected to pickling, annealing or the like step.
  • the steel sheet having the above-mentioned chemical composition is subjected to a primary step (1) of subjecting to primary heat treatment and subsequent cooling to make the structure of the steel sheet into a structure comprising martensite; a secondary step (2) of performing secondary heat treatment in a continuous galvanizing line, so as to temper martensite made by the primary heat treatment, and again austenitize a part of the structure of the steel sheet in order to generate retained austenite and a low-temperature transformation phase after cooling; and a subsequent tertiary step (3) of performing galvanization, thereby coming to a high-strength galvanized steel sheet excellent in ductility,
  • the steel sheet is subjected to primary heat treatment in which the steel sheet is held at a temperature of (Ac 3 transformation temperature -50°C) or higher for at least 5 seconds or more, and then the steel sheet is rapidly cooled to a temperature that is not more than Ms point temperature at a cooling rate of 10 °C/sec. or more.
  • This primary step causes production of 20% or more (by volume) of lath-like martensite in the steel sheet.
  • the heating and holding temperature in the primary heat treatment is below (Ac 3 transformation temperature -50°C), or the holding time is below 5 sec., the amount of austenite produced in the heating and holding is small so that the amount of lath-like martensite obtained after cooling becomes insufficient.
  • the cooling rate after the primary heat treatment is below 10 °C/sec., the structure of the steel sheet after the cooling cannot be made to a structure comprising lath-like martensite.
  • the upper limit of cooling rate after the primary heat treatment is preferably set to 100 °C/sec. or less.
  • the holding time is preferably set to from not less than 5 sec. to not more than 120 sec.
  • this primary step may be replaced by a step in which the cooling after the final hot rolling is set up to rapid cooling to not more than Ms point temperature at a cooling rate of 10 °C/sec. or more.
  • the steel sheet in which 20% or more of lath-like martensite has been produced by the primary step is subjected to secondary heat treatment in which the steel sheet is held within a temperature range (between Ac 1 transformation temperature and Ac 3 transformation temperature) for 5 to 120 sec., and then the steel sheet is cooled to a temperature that is 500°C or lower at a cooling rate of 5°C/sec. or more.
  • the lath-like martensite produced by the primary step is made to the tempered martensite and further a part of the structure of the steel sheet is again austenitized in order to produce retained austenite and the low-temperature transformation phase finally.
  • This secondary step is preferably performed in a continuous galvanizing line having both of annealing equipment and galvanizing equipment.
  • the heating and holding temperature in the secondary heat treatment is below Ac 1 transformation temperature, austenite is not regenerated and retained austenite or the low-temperature transformation phase cannot be obtained after the cooling. If the holding temperature is over Ac 3 transformation, the tempered martensite is again austenitized.
  • the cooling rate until 500°C after the secondary heat treatment is below 5 °C/sec., the cooling rate is slow so that the austenite produced in the secondary heat treatment is not turned to retained austenite or the low-temperature transformation phase but is transformed to ferrite, perlite or the like.
  • the cooling rate after the secondary heat treatment is preferably from not less than 5 °C/sec. to not more than 50 °C/sec.
  • This secondary step is preferably performed in a continuous galvanizing line having both of annealing equipment and galvanizing equipment.
  • the present process can be shifted to a tertiary step immediately after the secondary step.
  • productivity is improved.
  • the steel sheet that has been subjected to the secondary step is subjected to galvanizing treatment and then cooled to 300°C at a cooling rate of 5°C/sec. or more.
  • the galvanizing treatment may be performed under usual treatment conditions in a continuous galvanizing line. The conditions are not especially limited. However, in galvanizing treatment at extremely high temperatures, it becomes difficult to keep a necessary amount of retained austenite. For this reason, the galvanization is preferably performed at 500°C or lower. When the cooling rate after the galvanization is extremely small, it becomes difficult to keep a necessary amount of retained austenite. Therefore, the cooling rate within a temperature range from a temperature after the galvanizing treatment to 300°C is preferably limited to 5 °C/sec. or more. Preferably, the cooling rate is 50 °C/sec. or less. Of course, after the galvanizing treatment, wiping for adjusting the coating-weight may be performed if necessary.
  • alloying treatment may be conducted.
  • the steel sheet after the galvanizing treatment is again heated to a temperature range of 450 to 550 °C and then the galvanized layer is alloyed.
  • cooling is preferably conducted to 300 °C at a cooling rate of 5 °C/sec. or more. Alloying treatment at high temperatures makes it difficult to keep a necessary amount of retained austenite, so that the ductility of the steel sheet deteriorates. Therefore, the upper limit of alloying temperature is preferably limited to 550°C. If the alloying temperature is below 450°C, the alloying advances slowly so that productivity drops. If the cooling rate after the alloying treatment is extremely low, it becomes difficult to keep necessary retained austenite. Therefore, it is preferred to limit the cooling rate for a temperature range from a temperature after the alloying treatment to 300°C to 5 °C /sec. or more.
  • the steel sheet after the galvanizing treatment or the alloying treatment may be subjected to temper rolling in order to reform its shape or adjust surface-roughness or the like. If the steel sheet is subjected to such treatment as resin coating, oil and grease coating or any one of various coatings, no inconvenience arises.
  • the present invention is carried out on the assumption that the secondary heating, the galvanizing treatment and the alloying treatment of steel sheet are performed in a continuous galvanizing line having annealing equipment, galvanizing equipment and alloying equipment.
  • each of the steps may be carried out in independent equipment or an independent step.
  • Molten steels having the compositions shown in Table 1 were manufactured to in a steel converter. They were made into slabs by continuous casting. The resultant slabs were hot rolled to have a thickness of 2.6 mm. Next, they were pickled and then cold rolled to obtain steel sheets having a thickness of 1.0 mm.
  • these cold-rolled steel sheets were subjected to a primary step wherein heating and holding and then cooling were performed under primary step conditions shown in Table 2 in a continuous annealing line. After the primary step, their structures were examined to measure the amount of lath-like martensite. Further, these steel sheets that had been subjected to the primary step were subjected to a secondary step wherein heating and holding and then cooling were performed under secondary step conditions shown in Table 2 in a continuous galvanizing line, and subsequently the steel sheets were subjected to tertiary step wherein galvanizing treatment and cooling were performed, and some of the steel sheets were subjected to the alloying treatment of their galvanized layers, in which reheating was performed after the galvanizing treatment. The resultant steel sheets were examined about their microstructure and mechanical properties. The results are shown in Table 3.
  • the galvanizing treatment was conducted by immersing the steel sheets in a galvanizing tank whose bath temperature was 475°C. The steel sheets were pulled up and then their coating-weight was adjusted by gas-wiping in the manner that their coating-weight on their single surface would be 50 g/m 2 . In the case that their galvanized layer was subjected to the alloying treatment, after the wiping, the temperature of the steel sheets was raised to 500°C at a heating rate of 10 °C/sec. The holding time upon the alloying treatment was adjusted in the manner that the iron content in each galvanized layer would be 9-11%.
  • Intensity ratios of diffracted X-ray at ⁇ 111 ⁇ , ⁇ 200 ⁇ , ⁇ 220 ⁇ and ⁇ 311 ⁇ planes of the retained austenite phase in the specimens were obtained respectively, and the average value thereof was defined as the volume ratio of retained austenite.
  • yield strength (yield point) YP Yield point
  • tensile strength TS tensile strength TS
  • elongation El were measured with JIS No. 5 tensile test pieces taken out, in the direction perpendicular to the rolling direction, from the steel sheets.
  • Examples of the present invention were high-ductility and high-strength galvanized steel sheets with well-balanced strength and elongation, having a tensile strength TS of 590 MPa or more, an elongation El of 30% or more, and a strength-elongation balance (TS ⁇ El) of 21000 MPa % or more.
  • Comparative Examples which were out of the scope of the present invention, had insufficient ductility and low strength-elongation balance.
  • Molten steel B having the composition shown in Table 1 was produced to in a steel converter.
  • the steel was made into slabs by continuous casting.
  • the resultant slabs were subjected to a hot rolling step for making their thickness to 2.3 mm.
  • a hot-rolled steel sheet structure adjusting step in which they were rapidly cooled under conditions shown in Table 4 and wound into a coil form.
  • This hot-rolled steel sheet structure adjusting step was performed instead of the primary step in the manufacturing method of the present invention.
  • the microstructure of the steel sheet was examined to measure the amount of lath-like martensite.
  • this hot-rolled steel sheet was subjected to a secondary step wherein heating and holding and then cooling were performed under secondary step conditions shown in Table 4 in a continuous galvanizing line. Subsequently, the steel sheet was subjected to a tertiary step of performing galvanizing treatment, alloying treatment of the galvanized layer, and cooling.
  • the galvanizing treatment was performed in the same manner as in Example 1.
  • About the resultant steel sheet, its microstructure and mechanical properties were examined in the same manner as in Example 1. The results are shown in Table 5.
  • the galvanized steel sheet of the present invention was a high-strength galvanized steel sheet excellent in ductility, having a tensile strength TS of 590 MPa or more and a strength-elongation balance (TS ⁇ El) of 23000 MPa % or more.
  • any high-strength galvanized steel sheet thereof has very good ductility. It is possible to produce cheaply and stably a high-strength galvanized steel sheet which is very suitable for a raw material of forming products, typical examples of which are car parts. Thus, the present invention has remarkably advantageous effect for industries.

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Claims (4)

  1. Hochfestes galvanisiertes Stahlblech mit hervorragender Duktilität, dadurch gekennzeichnet, dass es eine galvanisierte Schicht oder legierte galvanisierte Schicht auf der Oberfläche eines Stahlblechs umfasst; wobei das Stahlblech eine Zusammensetzung aufweist, die umfasst: C: 0, 05 - 0,20 Masse-%, Si: 0,3 - 1,8 Masse-%, Mn: 1,0 - 3,0 Masse-%, optional eine oder mehrere Gruppen, die aus den folgenden Gruppen (a) - (d) ausgewählt sind:
    (a-Gruppe): ein oder zwei Bestandteile, die aus Cr und Mo ausgewählt sind, in einer Gesamtmenge von 0,05 - 1,0 Masse-%,
    (b-Gruppe): B: 0,003 Masse-% oder weniger,
    (c-Gruppe): ein oder mehrere Bestandteile, die aus Ti, Nb und V ausgewählt sind, in einer Gesamtmenge von 0,01 - 0, 1 Masse-%, und
    (d-Gruppe): ein oder zwei Bestandteile, die aus Ca und Seltenerdmetallen ausgewählt sind, in einer Gesamtmenge von 0,01 Masse-% oder weniger;

    zum Rest Fe und beiläufige Verunreinigungen,
    und das Stahlblech eine Verbundstruktur mit angelassenem Martensit, zurückbehaltenem Austenit, Ferrit und einer Niedertemperaturtransformationsphase umfasst, wobei der angelassene Martensit in einer Menge von 20 oder mehr Vol.-% enthalten ist und der zurückbehaltene Austenit in einer Menge von 2 oder mehr Vol.-% enthalten ist.
  2. Verfahren zur Herstellung eines hochfesten galvanisierten Stahlblechs mit hervorragender Duktilität, das gekennzeichnet ist durch die aufeinanderfolgende Durchführung einer ersten Stufe der Durchführung einer ersten Wärmebehandlung eines Stahlblechs mit einer Zusammensetzung, die umfasst: C: 0,05 - 0,20 Masse-%, Si: 0,3 - 1,8 Masse-%, Mn: 1,0 - 3,0 Masse-%, optional eine oder mehrere Gruppen die aus den im Folgenden angegebenen Gruppen (a) - (d) ausgewählt sind:
    (a-Gruppe): ein oder zwei Bestandteile, die aus Cr und Mo ausgewählt sind, in einer Gesamtmenge von 0,05 - 1,0 Masse-%,
    (b-Gruppe): B: 0,003 Masse-% oder weniger,
    (c-Gruppe): ein oder mehrere Bestandteile, die aus Ti, Nb und V ausgewählt sind, in einer Gesamtmenge von 0,01 - 0,1 Masse-%, und
    (d-Gruppe): ein oder zwei Bestandteile, die aus Ca und Seltenerdmetallen ausgewählt sind, in einer Gesamtmenge von 0,01 Masse-% oder weniger;

    zum Rest Fe und beiläufige Verunreinigungen,
    wobei das Stahlblech 5 s oder länger bei einer Temperatur von (Ac3-Transformationstemperatur - 50 °C) oder höher gehalten wird und das Stahlblech dann auf eine Temperatur, die nicht höher als die Ms-Punkttemperatur ist, mit einer Kühlrate von 10 °C/s oder mehr gekühlt wird; einer zweiten Stufe der Durchführung einer zweiten Wärmebehandlung des Stahlblechs, wobei das Stahlblech in einem Temperaturbereich zwischen der Ac1-Transformationstemperatur und der Ac3-Transformationstemperatur während 5 - 120 s gehalten wird und das Stahlblech dann auf eine Temperatur, die 500 °C oder niedriger ist, mit einer Kühlrate von 5 °C/s oder mehr gekühlt wird; und der anschließenden dritten Stufe der Durchführung einer Galvanisierungsbehandlung des Stahlblechs zur Bildung einer galvanisierten Schicht auf der Oberfläche des Stahlblechs und des anschließenden Kühlens des Stahlblechs auf 300 °C mit einer Kühlrate von 5 °C/s oder mehr.
  3. Verfahren zur Herstellung eines hochfesten galvanisierten Stahlblechs mit hervorragender Duktilität nach Anspruch 2, das gekennzeichnet ist durch die dritte Stufe der Durchführung einer Galvanisierungsbehandlung des Stahlblechs zur Bildung der galvanisierten Schicht auf der Oberfläche des Stahlblechs, das abermalige Erhitzen des Stahlblechs auf einen Temperaturbereich von 450 °C bis 550 °C zur Durchführung einer Legierungsbehandlung der galvanisierten Schicht und das Kühlen des Stahlblechs nach der Legierungsbehandlung auf 300 °C mit einer Kühlrate von 5 °C/s oder mehr.
  4. Verfahren zur Herstellung eines hochfesten galvanisierten Stahlblechs mit hervorragender Duktilität nach einem der Ansprüche 2 oder 3, das dadurch gekennzeichnet ist, dass das Stahlblech zu einem warmgewalzten Stahlblech gemacht wird, das einem Endwarmwalzen bei einer Temperatur von (Ar3-Transformationstemperatur - 50 °C) oder höher unterzogen wurde, und die im Vorhergehenden genannte erste Stufe durch eine Stufe der Einstellung der Struktur des warmgewalzten Stahlblechs unter raschem Kühlen des Stahlblechs auf eine Temperatur, die die Ms-Punkttemperatur oder niedriger ist, mit einer Kühlrate von 10 °C/s oder mehr nach dem Endwarmwalzen ersetzt wird.
EP00919136A 1999-04-21 2000-04-19 Hochfeste heisstauchzinkbeschichtete stahlplatte mit hervorragenden duktilitätseigenschaften und verfahren zu deren herstellung Expired - Lifetime EP1096029B1 (de)

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JPH06108152A (ja) 1992-09-30 1994-04-19 Kobe Steel Ltd 曲げ加工性に優れた高強度溶融亜鉛めっき鋼板の製造方法
JP2660644B2 (ja) * 1992-11-02 1997-10-08 新日本製鐵株式会社 プレス成形性の良好な高強度鋼板
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US6312536B1 (en) * 1999-05-28 2001-11-06 Kabushiki Kaisha Kobe Seiko Sho Hot-dip galvanized steel sheet and production thereof

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CN101415846B (zh) * 2006-01-10 2011-12-14 Sms西马格股份公司 调节多相钢的目标特性组合的方法和设备
DE102006019567B3 (de) * 2006-04-27 2007-11-08 Daimlerchrysler Ag Verfahren zum Herstellen umgeformter Stahlbauteile

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KR100638543B1 (ko) 2006-10-26
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CA2334672C (en) 2009-09-22
US6423426B1 (en) 2002-07-23
DE60025711T2 (de) 2006-09-14
EP1096029A1 (de) 2001-05-02
AU3987400A (en) 2000-11-10
KR20010043874A (ko) 2001-05-25
CA2334672A1 (en) 2000-11-02
WO2000065119A1 (fr) 2000-11-02

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